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CN111511949B - Hot-rolled steel sheet having excellent expansibility and method for producing same - Google Patents

Hot-rolled steel sheet having excellent expansibility and method for producing same Download PDF

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Publication number
CN111511949B
CN111511949B CN201880082627.2A CN201880082627A CN111511949B CN 111511949 B CN111511949 B CN 111511949B CN 201880082627 A CN201880082627 A CN 201880082627A CN 111511949 B CN111511949 B CN 111511949B
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hot
phase
cooling
steel sheet
rolled steel
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CN111511949A (en
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罗贤择
徐石宗
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Posco Holdings Inc
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Posco Co Ltd
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    • C—CHEMISTRY; METALLURGY
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    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
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    • B23K11/00—Resistance welding; Severing by resistance heating
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    • B23K31/00—Processes relevant to this subclass, specially adapted for particular articles or purposes, but not covered by only one of the preceding main groups
    • B23K31/02—Processes relevant to this subclass, specially adapted for particular articles or purposes, but not covered by only one of the preceding main groups relating to soldering or welding
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    • C21D8/0447—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the heat treatment
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    • C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
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    • B23K2101/00—Articles made by soldering, welding or cutting
    • B23K2101/04—Tubular or hollow articles
    • B23K2101/06—Tubes
    • B—PERFORMING OPERATIONS; TRANSPORTING
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    • B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
    • B23K2103/00—Materials to be soldered, welded or cut
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    • C21D2211/00—Microstructure comprising significant phases
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  • Metallurgy (AREA)
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Abstract

The present invention relates to a steel used for an automobile chassis part, and more particularly, to a hot-rolled steel sheet for a high-strength electric resistance welded steel pipe having excellent expansibility, in which a decrease in strength of a weld Heat Affected Zone (HAZ) formed when the hot-rolled steel sheet is electric resistance welded is small as compared with a base material, and a method for manufacturing the same.

Description

Hot-rolled steel sheet having excellent expansibility and method for producing same
Technical Field
The present invention relates to a steel used for automobile chassis parts and the like, and more particularly, to a hot-rolled steel sheet for electric resistance welded steel pipes having excellent expansibility and a method for manufacturing the same.
Background
In recent years, in order to ensure fuel efficiency regulations for protecting the global environment and collision safety of passengers, the automobile industry is expanding to use high-strength steel materials that can ensure both fuel efficiency and collision safety at a relatively low cost. This trend toward weight reduction is being developed in both vehicle bodies and chassis components.
In general, physical properties required for steel materials for vehicle bodies include strength, elongation for molding, spot weldability (spot welding) required for assembly, and the like.
In addition, due to the characteristics of the parts, the steel material used for the chassis parts requires arc weldability to be applied when assembling the parts and fatigue characteristics to ensure the durable quality of the parts, in addition to strength and elongation required for forming.
In particular, among chassis members, members such as Coupled Torsion Beam Axles (CTBA) are molded into hollow tubes and used in order to ensure strength and weight reduction at the same time, and high strength of materials is also being achieved in order to further reduce weight.
The material used as the pipe member as described above is generally used to manufacture a pipe by resistance welding, and therefore, in addition to resistance weldability, roll formability of the material at the time of manufacturing the pipe and cold formability after manufacturing the pipe are very important. Therefore, in terms of physical properties required for such materials, it is very important to ensure stability of the welded portion at the time of resistance welding. The reason for this is that, in the forming of electric resistance welded steel pipes, most of the fractures are concentrated in the welded portion or the weld heat affected zone due to deformation as compared with the base material.
In order to provide excellent roll formability to a material in the production of a pipe, it is advantageous that the yield ratio of the material is as low as possible, but when the material is a high-strength steel material, the yield strength is high and the yield ratio is high, so that spring back (spring back) is serious when roll forming is performed, and there is a problem that it is difficult to ensure roundness.
Also, in order to finally perform cold forming using a pipe, it is also necessary to secure elongation of the material, and in order to satisfy such a condition, a steel material having a low yield ratio and excellent elongation is basically required. A representative material that can satisfy such characteristics is a low yield ratio hot rolled steel sheet called Dual Phase (DP) steel.
The conventional low yield ratio hot rolled steel sheet is generally a ferrite-martensite dual phase composite structure steel, and exhibits a continuous yield behavior and low yield strength characteristics due to mobile dislocations introduced during martensitic transformation, and has excellent elongation characteristics.
In order to ensure such physical properties, conventionally, a composition system containing a large amount of Si in steel has been controlled in order to stably ensure the ferrite fraction when cooling after hot rolling. However, when a pipe is produced by the resistance welding method, a large amount of Si oxide is formed in a molten portion, and thus a problem occurs in that a gray scale (scratch) defect is caused in a welded portion. Further, if martensite is obtained by rapid cooling to the martensite start temperature (Ms) or less after ferrite transformation, and in this case, if the residual phase (phase) is composed of only pure martensite, there is a problem that the strength is greatly reduced by heat during welding. In particular, the reduction in hardness (Δ Hv) in the welding heat affected zone exceeds 30.
In addition, as a method for reducing the phenomenon of the hardness decrease as described above, when a pure bainite phase is obtained by rapidly cooling to a bainite transformation start temperature (Bs) or less after ferrite transformation, there is a problem that the yield strength increases and the elongation decreases although the decrease in hardness can be reduced.
(patent document 1) Japanese laid-open patent publication No. 2000-063955
Disclosure of Invention
Technical problem to be solved
An aspect of the present invention provides a hot-rolled steel sheet for a high-strength electric resistance welded steel pipe having excellent expansibility, which is less in a decrease in strength of a weld Heat Affected Zone (HAZ) formed when electric resistance welding is performed, compared to a base material, and a method for manufacturing the same.
Technical scheme
One aspect of the present invention provides a hot-rolled steel sheet for electric resistance welded steel pipes having excellent expansibility, characterized by comprising, in wt%: carbon (C): 0.15-0.22%, silicon (Si): 0.1-1.0%, manganese (Mn): 0.8-1.8%, phosphorus (P): 0.001-0.03%, sulfur (S): 0.001-0.01%, acid-soluble aluminum (sol. al): 0.001-0.19%, chromium (Cr): 0.3-1.0%, titanium (Ti): 0.01-0.05%, niobium (Nb): 0.025% or less, vanadium (V): 0.035% of nitrogen (N): 0.001 to 0.01%, and the balance being Fe and other unavoidable impurities, wherein the Mn and Si satisfy the following relational expression 1, the microstructure comprises a ferrite phase as a matrix structure and a hard phase composed of a martensite phase and a bainite phase mixed together, the fraction of crystal grains in which the martensite phase and the bainite phase are mixed together in one crystal grain (single grain) in the total fraction (area fraction) of the hard phase is 50% or more, and the carbon distribution in the crystal grains satisfies the following relational expression 2.
[ relational expression 1]
4<Mn/Si<12
(wherein Mn and Si represent the weight contents of the respective elements.)
[ relational expression 2]
1.2≤PCB/PCC≤2.0
(wherein, PCBRefers to a measurement value of the EPMA strength (intensity) of carbon in the hard phase at a position 70% of the corresponding distance from the center of a grain in which a martensite phase and a bainite phase are mixed to the boundary of the grain, PCCRefers to a measurement of the EPMA strength (intensity) of carbon at the center position of the same crystal grain. )
Another aspect of the present invention provides a method of manufacturing a hot rolled steel sheet for an electric resistance welded steel pipe having excellent expansibility, the method comprising the steps of: reheating the steel billet which meets the alloy composition and the relation 1 in the temperature range of 1180-1300 ℃; finish hot rolling the reheated slab at a temperature of Ar3 or higher to produce a hot-rolled steel sheet; cooling the hot rolled steel plate to a temperature range of 550 ℃ and 750 ℃ at a cooling rate of 20 ℃/second or more for one time; after the primary cooling, performing secondary cooling at a cooling rate of 0.05-2.0 ℃/sec within a range satisfying the following relational expression 3; after the secondary cooling, carrying out tertiary cooling at a cooling speed of more than 20 ℃/second, and cooling to a temperature range from normal temperature to 400 ℃; and after the third cooling, winding.
[ relational expression 3]
0≤t-ta≤3
(said [ ta ═ 250+ (65.1[ C)])+(9.2[Mn])+(20.5[Cr])-(4.7[Si]) - (4.8[ acid-soluble aluminium (Sol. Al)])-(0.87Temp)+(0.00068Temp^2)]Where t represents the retention time (sec) of the secondary cooling, ta represents the retention time (sec) of the secondary cooling for securing the optimum phase fraction, and Temp represents the intermediate temperature of the secondary cooling and representsThe temperature at the intermediate point between the starting point and the ending point of the secondary cooling. Each alloy component represents a weight content. )
Another aspect of the present invention provides an electric resistance welded steel pipe having excellent weldability, which is produced by electric resistance welding the hot-rolled steel sheet.
Advantageous effects
According to the present invention, it is possible to provide a hot-rolled steel sheet having a high strength and a low yield ratio with a tensile strength of 980MPa or more, which can suppress weld defects and minimize a decrease in hardness in a weld heat affected zone when resistance welding is performed on the hot-rolled steel sheet.
Further, when the pipe is manufactured and expanded after welding, cracks are not generated in the welded portion, the weld heat affected zone, or the like, and excellent cold formability can be secured.
Drawings
Fig. 1 shows a photograph (a) of observing the shape of a structure accounting for 50% or more by area ratio in the total hard phase of invention example 1 in one embodiment of the present invention using an electron Probe X-ray microanalyzer (EPMA) and a distribution (b) of measuring the carbon (C) content of each region of the above-described structure.
Fig. 2 shows a photograph (a) of the shape of a hard phase structure of a conventional DP steel observed using an electron Probe X-ray microanalyzer (EPMA) and a distribution (b) of the carbon (C) content measured in each region of the above structure.
Best mode for carrying out the invention
The present inventors have conducted intensive studies to manufacture a 980MPa grade hot rolled steel sheet excellent in cold formability, which has a yield ratio controlled to less than 0.8, and thus is easy to roll form for pipe manufacture, and which has excellent resistance weldability and a small decrease in strength in a weld heat affected zone, and thus does not cause fracture in the weld zone or the heat affected zone when subjected to expansion working after pipe manufacture.
As a result, it was confirmed that a hot-rolled steel sheet for electric resistance welded steel pipes having high strength and excellent expansibility can be provided by forming a fine structure advantageous for ensuring the above physical properties by optimizing the alloy composition and the production conditions of the steel material, and the present invention was completed.
The present invention will be described in detail below.
The hot-rolled steel sheet for an electric resistance welded steel pipe excellent in expansibility according to one aspect of the present invention preferably contains, in terms of weight%, carbon: (C) the method comprises the following steps 0.15-0.22%, silicon (Si): 0.1-1.0%, manganese (Mn): 0.8-1.8%, phosphorus (P): 0.001-0.03%, sulfur (S): 0.001-0.01%, acid-soluble aluminum (sol. al): 0.001-0.19%, chromium (Cr): 0.3-1.0%, titanium (Ti): 0.01-0.05%, niobium (Nb): 0.025% or less, vanadium (V): 0.035% of nitrogen (N): 0.001-0.01%.
The reason why the alloy composition of the hot-rolled steel sheet provided in the present invention is limited as described above will be described in detail below. At this time, the content of each element is weight% unless otherwise specified.
C：0.15-0.22％
Carbon (C) is the most economical and effective element for strengthening steel, and when the amount of added carbon is increased, the fraction of low-temperature phase-change phases such as bainite and martensite in the composite-structure steel composed of ferrite, bainite, and martensite increases, thereby improving tensile strength.
In the present invention, when the content of C is less than 0.15%, it is difficult to form a low-temperature phase change phase in the cooling process after hot rolling, and thus a desired level of strength cannot be secured. On the other hand, when the content of C exceeds 0.22%, the strength excessively increases, and there is a problem that weldability, formability, and toughness decrease.
Therefore, in the present invention, the content of C may be preferably controlled to 0.15 to 0.22%, and more preferably, the content of C may be controlled to 0.17 to 0.21%.
Si：0.1-1.0％
Silicon (Si) has an effect of deoxidizing molten steel and of solid solution strengthening, and silicon is a ferrite stabilizing element and has an effect of promoting ferrite transformation when cooling after hot rolling. Therefore, the silicon is an effective element for increasing the ferrite fraction of the matrix constituting the steel having a ferrite, bainite, and martensite composite structure.
When the content of Si is less than 0.1%, the ferrite stabilizing effect is small, and it is difficult to form a matrix structure with a ferrite structure. On the other hand, if the Si content exceeds 1.0%, red scale due to Si is formed on the surface of the steel sheet during hot rolling, which not only deteriorates the surface quality of the steel sheet but also deteriorates ductility and electric resistance weldability.
Therefore, in the present invention, the content of Si may be preferably controlled to 0.1 to 1.0%, and more preferably, the content of Si may be controlled to 0.15 to 0.8%.
Mn：0.8-1.8％
As Si, manganese (Mn) is an effective element for solid solution strengthening of steel and increases hardenability of steel, and thus a bainite phase or a martensite phase is easily formed upon cooling after hot rolling.
However, when the content of manganese is less than 0.8%, the above-described effect cannot be sufficiently obtained. On the other hand, if the content of manganese exceeds 1.8%, ferrite transformation is excessively delayed, so that it is difficult to secure an appropriate fraction of the ferrite phase, and when a slab is cast in a continuous casting process, segregation portions are greatly developed at the thickness center portion, so that there is a problem that the resistance weldability of the final product is impaired.
Therefore, in the present invention, the content of Mn is preferably controlled to 0.8 to 1.8%, and more preferably to 1.0 to 1.75%.
P：0.001-0.03％
Phosphorus (P) is an impurity present in steel, and when the content of phosphorus exceeds 0.03%, ductility is reduced due to micro-segregation, and impact characteristics of steel are deteriorated. However, in order to make the content of P less than 0.001%, a large amount of time is required for steel-making operation, and there is a problem that productivity is greatly lowered.
Therefore, in the present invention, the content of P is preferably controlled to 0.001 to 0.03%.
S：0.001-0.01％
Sulfur (S) is an impurity present in steel, and when the content of sulfur exceeds 0.01%, it combines with Mn and the like to form a non-metallic inclusion, thereby having a problem of greatly reducing the toughness of steel. However, in order to make the S content less than 0.001%, a large amount of time is required for steel making operation, and there is a problem that productivity is lowered.
Therefore, in the present invention, the content of S is preferably controlled to 0.001 to 0.01%.
Acid-soluble aluminum (sol. al): 0.001-0.19%
Al is a ferrite stabilizing element and is an element effective for forming a ferrite phase when cooling is performed after hot rolling.
When the content of such acid-soluble aluminum (sol. al) is less than 0.001%, the addition effect thereof is insufficient, so that the above-mentioned effect cannot be sufficiently obtained, and a large amount of time is required for the steel-making operation, so that there is a problem in that productivity is significantly reduced. On the other hand, when the content of acid-soluble aluminum (sol. Al) exceeds 0.19%, Al-based oxides (e.g., Al) having a relatively high melting point are easily formed during resistance welding2O3) Therefore, stress is locally concentrated around the inclusions during expansion, and this may cause the initiation of cracks.
Therefore, in the present invention, the content of the acid-soluble aluminum (sol. al) may be preferably controlled to 0.001 to 0.19%, more preferably, the content of the acid-soluble aluminum (sol. al) may be controlled to 0.003 to 0.15%, and further preferably, the content of the acid-soluble aluminum (sol. al) may be controlled to 0.003 to 0.10%.
Cr：0.3-1.0％
Chromium (Cr) solid-solution strengthens the steel, and like Mn, chromium delays the transformation of the ferrite phase upon cooling, thereby acting to facilitate the formation of martensite.
When the content of Cr is less than 0.3%, the above-described effect cannot be sufficiently obtained. On the other hand, when the content of Cr exceeds 1.0%, ferrite transformation is excessively delayed, so that the fraction of a low-temperature phase transformation phase such as a bainite phase or martensite phase increases to a desired fraction or more, thereby having a problem of rapid deterioration of elongation.
Therefore, in the present invention, the content of Cr may be preferably controlled to 0.3 to 1.0%, and more preferably, the content of Cr may be controlled to 0.4 to 0.8%.
Ti：0.01-0.05％
Titanium (Ti) combines with nitrogen (N) during continuous casting to form coarse precipitates, and a part of titanium remains in the material without being re-dissolved during reheating for the hot rolling process, and the precipitates that are not re-dissolved have a high melting point and cannot be re-dissolved during welding, and thus play a role in suppressing grain growth in the weld heat affected zone. Further, the re-dissolved Ti is finely precipitated in the transformation process in the cooling process after hot rolling, and thus has an effect of greatly improving the strength of the steel.
In order to sufficiently obtain the above-mentioned effects, it is preferable to contain 0.01% or more of Ti, but when the content of Ti exceeds 0.05%, the yield ratio of the steel becomes high due to fine precipitated precipitates, and there is a problem that it is difficult to perform roll forming in the production of a pipe.
Therefore, in the present invention, the content of Ti is preferably controlled to 0.01 to 0.05%.
Nb: less than 0.025% (except 0%)
Niobium (Nb) is an element that forms precipitates in the form of carbonitride to function to improve strength, and particularly precipitates that are finely precipitated in the phase transformation process in the cooling process after hot rolling greatly improve the strength of steel.
When the content of Nb exceeds 0.025%, the yield ratio of the steel is significantly increased, and it is difficult to roll-form the steel into a pipe, which is not preferable. Therefore, in the present invention, the content of Nb is preferably controlled to 0.025% or less, with the exception of 0%.
V: less than 0.035% (except 0%)
Vanadium (V) is an element that forms precipitates in the form of carbonitride to function to improve strength, and particularly precipitates finely precipitated in the phase transformation process in the cooling process after hot rolling greatly improve the strength of steel.
When the content of V exceeds 0.035%, the yield ratio of the steel is greatly increased, and it is difficult to perform roll forming in the production of a pipe, which is not preferable. Therefore, in the present invention, it is preferable to control the content of V to 0.035% or less except for 0%.
N：0.001-0.01％
Nitrogen (N) is a typical solid-solution strengthening element together with C, and forms coarse precipitates together with titanium, aluminum, and the like.
In general, N has a better solid solution strengthening effect than C, but has a problem of greatly decreasing toughness as the amount of N in steel increases, and therefore, in the present invention, it is preferable to limit the upper limit of N to 0.01%. However, when the N content is less than 0.001%, a large amount of time is required for the steel-making operation, and productivity is lowered.
Therefore, in the present invention, the content of N is preferably controlled to 0.001 to 0.01%.
In the present invention, manganese (Mn) and silicon (Si) controlled to the above contents preferably satisfy the following relational formula 1.
[ relational expression 1]
4<Mn/Si<12
(wherein Mn and Si represent the weight contents of the respective elements.)
When the value of the relational expression 1 is 4 or less or 12 or more, it is not preferable because excessive Si oxide or Mn oxide is formed in the welded portion when the electric resistance welded steel pipe is manufactured, and the incidence of gray scale (permanent) defects increases. This is because the melting point of the oxide generated in the molten portion when the electric resistance welded steel pipe is manufactured becomes high, and the probability of remaining in the welded portion during extrusion discharge increases.
Therefore, in the present invention, it is preferable that the above content range is satisfied and the relational expression 1 is satisfied.
The remainder of the composition of the present invention is iron (Fe). However, since impurities which are not required are inevitably mixed from the raw materials or the surrounding environment in a general manufacturing process, they cannot be excluded. These impurities are well known to the skilled person in the usual manufacturing process and therefore not specifically mentioned in the present specification for all of them.
The microstructure of the hot-rolled steel sheet of the present invention satisfying the alloy composition and the relational expression 1 described above preferably contains a ferrite phase as a matrix structure and a hard phase composed of martensite and bainite in combination.
In this case, the ferrite phase is preferably contained at 60 to 80% by area fraction. When the fraction of the ferrite phase is less than 60%, there is a possibility that the elongation of the steel is sharply reduced, while when the fraction of the ferrite phase exceeds 80%, the fraction of hard phases (bainite and martensite) is relatively reduced, and thus a desired strength cannot be secured.
Also, the hard phase of the present invention preferably contains grains in which a martensite (M) phase and a bainite (B) phase are present in a mixed state, that is, preferably contains grains in which an M phase and a B phase are present among prior austenite grains. Such crystal grains are more preferably contained by 50% or more in the total hard phase fraction (area fraction). The hard phase has a martensite single phase and/or a bainite single phase structure in addition to grains in which the M phase and the B phase are mixed.
In the explanation with reference to the drawings, fig. 1 is a photograph (a) of the structure of the inventive steel in one example of the present invention, specifically, a result (b) of measuring the crystal grains of the structure occupying 50% or more of the total hard phase by area ratio and the carbon content of each region of the crystal grains, and it can be confirmed that the carbon content around the grain boundary of the crystal grains is different from the carbon content in the central region. This means that in one crystal grain (single grain) in which a martensite phase and a bainite phase are mixed, a martensite phase exists around the grain boundary, and a bainite phase exists in the center.
Fig. 2 is a photograph (a) of the structure of a conventional steel having the structure of a conventional DP steel, that is, a result (b) of measuring martensite crystal grains accounting for 90% or more in terms of area ratio in the hard phase and the carbon content of the crystal grains. It was confirmed that the carbon distribution from the grain boundary to the center of the crystal grain was relatively uniform compared to the present invention.
As described above, unlike the conventional DP steel, the hot-rolled steel sheet according to the present invention has the effect of ensuring excellent expansibility of electric resistance welded steel pipe by introducing sufficient mobile dislocations into the boundary between the hard phase and the ferrite phase while sufficiently ensuring the bainite phase, thereby minimizing the decrease in hardness in the weld heat affected zone and achieving a low yield ratio.
More specifically, in the hot-rolled steel sheet according to the present invention, the fraction of crystal grains in which the martensite phase and the bainite phase are present in one crystal grain (single grain) in a mixed manner is preferably 50% or more in the total fraction (area fraction) of the hard phase, and the carbon distribution in the crystal grains preferably satisfies the following relational expression 2.
When the carbon distribution represented by the following relational expression 2 is less than 1.2, the crystal grains in which the martensite phase and the bainite phase are mixed cannot be realized in the hard phase, and the martensite single-phase structure is formed, so that the object of the present invention cannot be achieved. On the other hand, if the value of the carbon distribution represented by the following relational expression 2 exceeds 2.0, acicular martensite is formed around the grain boundaries of the crystal grains, and a ferrite phase is formed in the central region thereof instead of a bainite phase, so that there is a problem that the expansibility is greatly reduced.
[ relational expression 2]
1.2≤PCB/PCC≤2.0
(wherein, PCBRefers to a measurement value of EPMA strength of carbon in a hard phase at a position 70% of a corresponding distance from the center of a grain in which martensite phase and bainite phase are mixed to the boundary of the grain, PCCRefers to a measurement of the EPMA strength of carbon at the center position of the same crystal grain. )
As described above, the hot-rolled steel sheet of the invention, which satisfies the alloy composition, the relational expression 1, and the microstructure, has a tensile strength of 980MPa or more and can secure a yield ratio (YR ═ YS/TS) of 0.8 or less.
Further, when the hot-rolled steel sheet of the present invention is manufactured into a pipe, the expansion rate of the pipe can be secured to 85% or more with respect to the elongation of the hot-rolled steel sheet.
Hereinafter, a method for manufacturing a hot-rolled steel sheet for an electric resistance welded steel pipe excellent in expansibility according to another aspect of the present invention will be described in detail.
Briefly, the present invention can manufacture a desired hot rolled steel sheet by [ reheating of a slab, hot rolling, primary cooling, secondary cooling, tertiary cooling, and coiling ], and conditions of the respective steps are described in detail below.
[ reheating step ]
First, a steel slab satisfying the above alloy composition and the relation 1 is prepared, and then the steel slab is reheated preferably within a temperature range of 1180-1300 ℃.
When the reheating temperature is less than 1180 ℃, heat storage of the slab is insufficient, so that it is difficult to secure a temperature when hot rolling is subsequently performed, and it is difficult to eliminate segregation occurring when continuous casting by diffusion. In addition, since precipitates precipitated during continuous casting cannot be sufficiently re-dissolved, it is difficult to obtain a precipitation strengthening effect in a process after hot rolling. On the other hand, when the reheating temperature exceeds 1300 ℃, strength is reduced due to abnormal grain growth of austenite grains, and there is a problem of promoting tissue non-uniformity.
Therefore, in the present invention, the reheating of the slab is preferably performed at 1180-1300 ℃.
[ Hot Rolling procedure ]
The slab reheated as described above is preferably hot-rolled to produce a hot-rolled steel sheet. In this case, the finish hot rolling is preferably performed at a temperature of Ar3 (ferrite phase transformation start temperature) or higher.
When the temperature at the finish hot rolling is less than Ar3, ferrite transformation is performed and rolling is performed, and thus it is difficult to secure desired structure and physical properties, while when the temperature at the finish hot rolling exceeds 1000 ℃, there is a problem that scale defects on the surface increase.
Therefore, in the present invention, the finish hot rolling is preferably performed at a temperature in the range of Ar3-1000 ℃.
[ Primary Cooling step ]
The hot rolled steel sheet obtained by the hot rolling as described above is preferably cooled, and at this time, it is preferably cooled in stages.
First, the hot-rolled steel sheet is preferably cooled to a temperature range of 550 ℃ and 750 ℃ by primary cooling at a cooling rate of 20 ℃/sec or more.
When the primary cooling end temperature is less than 550 ℃, the microstructure in the steel mainly includes a bainite phase, so that a ferrite phase as a matrix structure cannot be obtained, and thus sufficient elongation and low yield ratio cannot be secured. On the other hand, when the primary cooling end temperature exceeds 750 ℃, coarse ferrite and pearlite structures are formed, and thus desired physical properties cannot be secured.
When the cooling is performed at a cooling rate of less than 20 ℃/sec to the above temperature range, transformation of ferrite and pearlite occurs during the cooling, and thus a desired level of hard phase cannot be secured. The upper limit of the cooling rate is not particularly limited, and may be appropriately selected in consideration of the cooling equipment.
[ Secondary Cooling step ]
It is preferable to cool the hot rolled steel sheet having completed the primary cooling in an extremely slow cooling section under a specific condition. More specifically, it is preferable to perform very slow cooling at a cooling rate of 0.05 to 2.0 ℃/sec within a range satisfying the following relational expression 3.
[ relational expression 3]
0≤t-ta≤3
(said [ ta ═ 250+ (65.1[ C)])+(9.2[Mn])+(20.5[Cr])-(4.7[Si]) - (4.8[ acid-soluble aluminium (Sol. Al)])-(0.87Temp)+(0.00068Temp^2)]Where t denotes a retention time (sec) of the secondary cooling, ta denotes a retention time (sec) of the secondary cooling for securing an optimum phase fraction, and Temp is an intermediate temperature of the secondary cooling, and denotes a temperature at an intermediate point between a start point and an end point of the secondary cooling. Each alloy component represents a weight content. )
The relational expression 3 is for obtaining a fine structure desired in the present invention, specifically for obtaining the aforementioned fine structure satisfying the relational expression 2, and particularly by optimizing the intermediate temperature (Temp) in the extremely slow cooling section and the holding time in the extremely slow cooling section, a structure in which a martensite phase and a bainite phase are mixedly present in 50% or more of the total fraction of a hard phase can be obtained, and the carbon distribution of the structure can be made to satisfy the above relational expression 2.
More specifically, when the transformation from the austenite phase to the ferrite phase occurs during the retention time (secondary cooling) in the primary cooling or very slow cooling stage, carbon diffuses into the retained austenite, and at this time, the intermediate temperature (Temp) and the retention time in the very slow cooling stage are controlled so as to satisfy the above relational expression 3, so that the carbon concentration rapidly increases only in the portion adjacent to the ferrite phase. When the cooling in the later stage is started in this state, a part of the steel is transformed into bainite and a part of the steel is transformed into martensite due to the difference in the carbon concentration, and therefore the structure satisfying the relational expression 2 can be secured.
When the above-mentioned relational expression 3 is not satisfied in controlling the secondary cooling, a structure in which a martensite phase and a bainite phase are mixed cannot be realized, and a general DP steel structure is formed, and a reduction range of hardness of a welding heat affected zone becomes large at the time of resistance welding, so that there is a problem that expansibility is deteriorated.
In addition, in controlling the secondary cooling, when the cooling rate exceeds 2.0 ℃/sec, a sufficient time for forming a carbon distribution in which a microstructure in which a martensite phase and a bainite phase are mixed can be formed in a hard phase cannot be secured, and on the other hand, when the cooling rate is less than 0.05 ℃/sec, the ferrite fraction excessively increases, and thus desired microstructure and physical properties cannot be secured.
[ three Cooling Steps ]
After the completion of the secondary cooling in the very slow cooling section, it is preferable to perform tertiary cooling at a cooling rate of 20 ℃/sec or more to cool the material to a temperature range of normal temperature to 400 ℃. Wherein the normal temperature is about 15-35 ℃.
When the tertiary cooling termination temperature exceeds 400 ℃, the temperature is Ms (martensite transformation start temperature) or higher, and therefore most of the remaining non-transformed phase is transformed into a bainite phase, and thus a fine structure satisfying relational expression 2 of the present invention cannot be obtained.
Further, when the cooling rate at the time of the tertiary cooling is less than 20 ℃/sec, an excessive bainite phase is formed, and thus the physical properties and the fine structure desired in the present invention cannot be obtained. The upper limit of the cooling rate is not particularly limited, and may be appropriately selected in consideration of the cooling equipment.
[ Rolling procedure ]
For the hot rolled steel sheet that is finished with the three-time cooling as described above, it is preferable to perform the rolling process at this temperature.
In addition, the present invention may further include the steps of: naturally cooling the rolled hot rolled steel plate to a temperature range from normal temperature to 200 ℃, then carrying out acid cleaning treatment to remove scale on the surface layer part, and then oiling. In this case, when the steel sheet temperature before pickling exceeds 200 ℃, the surface layer portion of the hot-rolled steel sheet is excessively pickled, and thus there is a problem that the roughness of the surface layer portion is deteriorated.
The present invention provides an electric resistance welded steel pipe produced by electric resistance welding of a hot-rolled steel sheet produced as described above, which has an effect of excellent expandability.
The present invention will be described in more detail below with reference to examples. However, it should be noted that the following examples are only for illustrating the present invention and are described in more detail, and are not intended to limit the scope of the present invention. This is because the scope of the present invention is determined by the contents recited in the claims and the contents reasonably derived therefrom.
Detailed Description
(examples)
After preparing slabs having the composition systems shown in table 1 below, each slab was heated to 1250 ℃, and then subjected to finish hot rolling (finish hot rolling temperatures shown in table 2) to manufacture a hot-rolled steel sheet having a thickness of 3 mmt. After that, the steel sheet was subjected to primary cooling at a cooling rate of 80 ℃/sec (the cooling end temperature is shown in table 2), then controlled cooling (secondary cooling) was performed at an intermediate temperature and a holding time of a very slow cooling zone shown in table 2, and then, three times at a cooling rate of 60 ℃/sec, cooled to room temperature, and then wound.
Each hot-rolled steel sheet manufactured as described above was photographed at 3000 times SEM photograph, and then the area fraction (area)%) of each phase (ferrite: F, martensite: M, bainite: B) was measured using an image analyzer (image analyzer). The distribution behavior of carbon (C) in the grains of the structure, which accounts for 50% or more of the total fraction of the hard phase, was measured by the line scanning (EPMA) method at 7000 times magnification at intervals of 20-35nm (Acc V: 15.0kV, Prob C: 1.009 e-007A).
For each hot-rolled steel sheet, a test piece of JIS5 was prepared, and a tensile test was performed at normal temperature at a deformation rate of 10 mm/min.
Then, after a pipe having a diameter of 101.6 Φ was produced by resistance welding using each hot-rolled steel sheet, an expansion test was performed in accordance with KS standard B ISO 8493 (metal material-pipe expansion test) or a standard equivalent thereto. At this time, the expansion ratio of the produced pipe is shown as the elongation with respect to the hot-rolled steel sheet.
The results of the above measurements are shown in table 3 below.
[ Table 1]
Figure BDA0002547732530000151
[ Table 2]
Figure BDA0002547732530000152
Figure BDA0002547732530000161
[ Table 3]
Figure BDA0002547732530000162
Figure BDA0002547732530000171
(in Table 3, ` F ` denotes a ferrite phase, ` P ` denotes a pearlite phase, ` M ` denotes a martensite phase, ` B ` denotes a bainite phase, YS denotes a yield strength, TS denotes a tensile strength, YR denotes a yield ratio (yield strength/tensile strength), and El denotes an elongation, wherein the area fraction of pearlite is 5% or less (including 0%))
(in Table 3, F + P represents the sum of the phase fractions of ferrite and pearlite, and 85% or more of the total F + P fractions represent ferrite phases.)
As shown in tables 1 to 3, it was confirmed that the alloy compositions, the composition relationships, and the production conditions all satisfy the conditions proposed by the present invention, and the desired fine structures were formed in invention examples 1 to 10, thereby obtaining the desired physical properties, and excellent expansion ratios of 85% or more were secured after the production of the pipe with respect to the elongation of the base material (hot-rolled steel sheet).
In addition, comparative examples 1 to 12 are cases where the alloy compositions restricted in the present invention are not satisfied.
However, in comparative example 1, the content of C was too large, and in comparative example 7, the content of Cr was too large, and it was confirmed that the ta values in the relational expression 3 were calculated to be 13 (sec) and 27 (sec), respectively. That is, comparative examples 1 and 7 require excessive holding time of the extremely slow cooling section (after cooling, ROT interval) for securing the optimum phase fraction, which is out of the range of the controllable holding time in the extremely slow cooling section of the present embodiment.
In comparative example 2 and comparative example 8, the contents of C and Cr were insufficient, respectively, and the ta value of relational expression 3 calculated in comparative example 2 and comparative example 8 was less than 1 (second), and hard phases were difficult to form when cooling was performed after hot rolling, and therefore, the fine structure (structure satisfying relational expression 2) desired in the present invention could not be secured.
In comparative examples 9 and 10, the content of acid-soluble aluminum (sol. al) that promotes ferrite transformation is too large, and thus a hard phase cannot be sufficiently secured, and thus a desired level of strength cannot be secured. Further, Al is formed in the welded portion2O3Such high melting point oxide inclusions have a problem that stress is locally concentrated around the inclusions at the time of expansion, and thus they become a factor for starting generation of cracks.
Comparative examples 3 and 4 are the case where the content of Si is out of the range of the present invention, comparative examples 5 and 6 are the case where the content of Mn is out of the range of the present invention, and the relationship between the contents of Mn and Si (corresponding to relational expression 1) is out of the range of the present invention or the t-ta value of relational expression 3 does not satisfy the range of the present invention, so that the possibility of occurrence of a gray spot defect at the welded portion at the time of welding is increased, and therefore cracks are likely to occur at the welded portion at the time of tube manufacturing and expansion. Actually, the comparative examples are inferior in expansibility.
Comparative examples 11 to 15 belong to steels satisfying the present invention in terms of alloy composition and relational expression 1, but in comparative example 11 and comparative example 12, the retention time at the time of secondary cooling was controlled to 15 seconds and 0 second, respectively, and it was confirmed that the t-ta value in relational expression 3 failed to satisfy the effective value. Further, it was confirmed that the t-ta value of relational expression 3 failed to satisfy the effective value because the primary cooling end temperature of comparative example 13 and comparative example 14 was out of the range of the present invention and the cooling rate at the time of secondary cooling of comparative example 15 exceeded 2.0 ℃/sec.
Since the distribution of carbon in the grains accounting for 50% or more of the total hard phase in the comparative examples 11 to 15 in terms of area ratio does not satisfy the relational expression 2 of the present invention, the expansion rate of 80% or more after the production of the pipe with respect to the elongation of the hot-rolled steel sheet cannot be secured.
In addition, in the present invention, no comparative example in which the content of acid-soluble aluminum (sol. al) is less than 0.001% is proposed, but in this case, a significant reduction in productivity is caused in terms of workability, which is well known to those skilled in the art.

Claims (7)

1. A hot-rolled steel sheet for electric resistance welded steel pipes having excellent expansibility, characterized by comprising in wt%: carbon (C): 0.15-0.22%, silicon (Si): 0.1-1.0%, manganese (Mn): 0.8-1.8%, phosphorus (P): 0.001-0.03%, sulfur (S): 0.001-0.01%, acid-soluble aluminum (sol. al): 0.001-0.19%, chromium (Cr): 0.3-1.0%, titanium (Ti): 0.01-0.05%, niobium (Nb): 0.025% or less, vanadium (V): 0.035% of nitrogen (N): 0.001 to 0.01%, and the balance of Fe and other unavoidable impurities, the Mn and Si satisfying the following relational formula 1,
the fine structure comprises a ferrite phase as a matrix structure and a hard phase composed of a martensite phase and a bainite phase mixed together, wherein the fraction of crystal grains in which the martensite phase and the bainite phase are mixed together in one grain is 50% or more of the total fraction of the hard phase in terms of area fraction, and the carbon distribution in the grains satisfies the following relational expression 2,
[ relational expression 1]
4<Mn/Si<12
Wherein Mn and Si represent the weight contents of the respective elements,
[ relational expression 2]
1.2≤PCB/PCC≤2.0
Wherein, PCBRefers to a measurement value of EPMA strength of carbon in a hard phase at a position 70% of a corresponding distance from the center of a grain in which martensite phase and bainite phase are mixed to the boundary of the grain, PCCRefers to a measurement of the EPMA strength of carbon at the center position of the same crystal grain.
2. The hot-rolled steel sheet for electric resistance welded steel pipe excellent in expansibility according to claim 1, wherein the ferrite phase is contained at 60 to 80% by area fraction.
3. The hot-rolled steel sheet for electric resistance welded steel pipes excellent in expansibility according to claim 1, wherein the hot-rolled steel sheet has a Tensile Strength (TS) of 980MPa or more and a yield ratio (YR ═ YS/TS) of 0.8 or less.
4. The hot-rolled steel sheet for electric resistance welded steel pipes excellent in expansibility according to claim 1, wherein after the hot-rolled steel sheet is manufactured into a pipe, the expansion rate of the pipe is 85% or more with respect to the elongation of the hot-rolled steel sheet.
5. A method for manufacturing a hot rolled steel sheet for an electric resistance welded steel pipe excellent in expansibility, comprising the steps of:
reheating a steel slab at a temperature in the range of 1180 ℃ 1300 ℃, said steel slab comprising in weight%: carbon (C): 0.15-0.22%, silicon (Si): 0.1-1.0%, manganese (Mn): 0.8-1.8%, phosphorus (P): 0.001-0.03%, sulfur (S): 0.001-0.01%, acid-soluble aluminum (sol. al): 0.001-0.19%, chromium (Cr): 0.3-1.0%, titanium (Ti): 0.01-0.05%, niobium (Nb): 0.025% or less, vanadium (V): 0.035% of nitrogen (N): 0.001 to 0.01%, and the balance of Fe and other inevitable impurities, the Mn and Si satisfying the following relational formula 1;
finish hot rolling the reheated slab at a temperature of Ar3 or higher to produce a hot-rolled steel sheet;
cooling the hot rolled steel plate to a temperature range of 550 ℃ and 750 ℃ at a cooling rate of 20 ℃/second or more for one time;
after the primary cooling, performing secondary cooling at a cooling rate of 0.05-2.0 ℃/sec within a range satisfying the following relational expression 3;
after the secondary cooling, carrying out tertiary cooling at a cooling speed of more than 20 ℃/second, and cooling to a temperature range from normal temperature to 400 ℃; and
after the cooling for the third time, the film is rolled,
[ relational expression 1]
4<Mn/Si<12
Wherein Mn and Si represent the weight contents of the respective elements,
[ relational expression 3]
0≤t-ta≤3
The [ ta + (65.1[ C +)])+(9.2[Mn])+(20.5[Cr])-(4.7[Si]) - (4.8[ acid-soluble aluminium (Sol. Al)])-(0.87Temp)+(0.00068Temp^2)]Where t denotes a retention time of the secondary cooling in seconds, ta denotes a retention time of the secondary cooling for securing an optimum phase fraction in seconds, Temp is an intermediate temperature of the secondary cooling, denotes a temperature at an intermediate point between a start point and an end point of the secondary cooling, and each alloy component denotes a weight content.
6. The method for manufacturing a hot-rolled steel sheet for an electric resistance welded steel pipe excellent in expansibility according to claim 5, wherein the finish hot rolling is performed at a temperature range of Ar3-1000 ℃.
7. An electric resistance welded steel pipe excellent in expansibility, which is produced by electric resistance welding the hot-rolled steel sheet according to claim 1.
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Family Cites Families (18)

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JPS595649B2 (en) 1979-10-03 1984-02-06 日本鋼管株式会社 Method for manufacturing high-strength hot-dip galvanized steel sheet with excellent workability
JPH07150247A (en) 1993-11-30 1995-06-13 Nkk Corp Production of steel tube with high strength and low yield ratio for construction use
JP3231204B2 (en) 1995-01-04 2001-11-19 株式会社神戸製鋼所 Composite structure steel sheet excellent in fatigue characteristics and method for producing the same
JP3716629B2 (en) 1998-08-12 2005-11-16 Ｊｆｅスチール株式会社 Manufacturing method of thin two-phase structure hot rolled steel strip
JP4881773B2 (en) * 2007-03-23 2012-02-22 株式会社神戸製鋼所 Low yield ratio high strength steel plate with excellent low temperature toughness of weld heat affected zone
JP5365217B2 (en) * 2008-01-31 2013-12-11 Ｊｆｅスチール株式会社 High strength steel plate and manufacturing method thereof
JP5200653B2 (en) * 2008-05-09 2013-06-05 新日鐵住金株式会社 Hot rolled steel sheet and method for producing the same
JP5446900B2 (en) * 2010-01-15 2014-03-19 Ｊｆｅスチール株式会社 High tensile hot-rolled steel sheet having high bake hardenability and excellent stretch flangeability and method for producing the same
JP5703678B2 (en) * 2010-05-31 2015-04-22 Ｊｆｅスチール株式会社 ERW steel pipe for oil well with excellent pipe expandability and its manufacturing method
CN103328671B (en) 2011-03-18 2015-06-03 新日铁住金株式会社 Hot-rolled steel sheet exhibiting exceptional press-molding properties and method for manufacturing same
JP5679452B2 (en) * 2011-08-17 2015-03-04 株式会社神戸製鋼所 High-strength hot-rolled steel sheet that combines formability and fatigue properties of the base metal and weld heat-affected zone
CN103732779B (en) * 2011-08-17 2015-11-25 株式会社神户制钢所 High tensile hot rolled steel sheet
CN104220619B (en) 2012-04-12 2016-08-24 杰富意钢铁株式会社 Thick hot-rolled steel sheet and manufacture method thereof for the rectangular steel tube towards building structural element
KR101439610B1 (en) * 2012-07-20 2014-09-11 주식회사 포스코 Low yield hot-rolled steel plate having excellent weldability and method for manufacturing thereof
KR101482342B1 (en) * 2012-12-26 2015-01-13 주식회사 포스코 High-strength hot-rolled steel plate having execellent weldability and bending workbility and method for manufacturing tereof
KR101630982B1 (en) * 2014-12-16 2016-06-16 주식회사 포스코 High strength hot rolled steel sheet having excellent bendability andbake hardenability and method for manufacturing thereof
JP6179584B2 (en) 2015-12-22 2017-08-16 Ｊｆｅスチール株式会社 High strength steel plate with excellent bendability and method for producing the same
KR101977487B1 (en) 2017-11-01 2019-05-10 주식회사 포스코 Hot rolled steel sheet with excellent weldability and method for manufacturing thereof

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